EP0621858B1 - Use of saline soluble inorganic fibres as insulation material - Google Patents

Use of saline soluble inorganic fibres as insulation material Download PDF

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Publication number
EP0621858B1
EP0621858B1 EP93902385A EP93902385A EP0621858B1 EP 0621858 B1 EP0621858 B1 EP 0621858B1 EP 93902385 A EP93902385 A EP 93902385A EP 93902385 A EP93902385 A EP 93902385A EP 0621858 B1 EP0621858 B1 EP 0621858B1
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EP
European Patent Office
Prior art keywords
fibres
fibre
shrinkage
mgo
sio
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP93902385A
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German (de)
English (en)
French (fr)
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EP0621858A1 (en
Inventor
Gary Anthony Jubb
Jean-Louis Martin
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Morgan Advanced Materials PLC
Original Assignee
Morgan Crucible Co PLC
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Priority claimed from GB929200993A external-priority patent/GB9200993D0/en
Priority claimed from GB929224612A external-priority patent/GB9224612D0/en
Application filed by Morgan Crucible Co PLC filed Critical Morgan Crucible Co PLC
Priority to EP01106342A priority Critical patent/EP1179513A1/en
Publication of EP0621858A1 publication Critical patent/EP0621858A1/en
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Publication of EP0621858B1 publication Critical patent/EP0621858B1/en
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C13/00—Fibre or filament compositions
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C2213/00—Glass fibres or filaments
    • C03C2213/02—Biodegradable glass fibres

Definitions

  • This invention relates to saline soluble, non-metallic, amorphous, inorganic oxide, refractory fibrous materials.
  • Inorganic fibrous materials are well known and widely used for many purposes (e.g. as thermal or acoustic insulation in bulk, mat, or blanket form, as vacuum-formed shapes, as vacuum formed boards and papers, and as ropes, yarns or textiles; as a reinforcing fibre for building materials; as a constituent of brake blocks for vehicles).
  • thermal or acoustic insulation in bulk, mat, or blanket form as vacuum-formed shapes, as vacuum formed boards and papers, and as ropes, yarns or textiles; as a reinforcing fibre for building materials; as a constituent of brake blocks for vehicles.
  • the properties for which inorganic fibrous materials are used require resistance to heat, and often resistance to aggressive chemical environments.
  • Inorganic fibrous materials can be either glassy or crystalline. Asbestos is an inorganic fibrous material one form of which has been strongly implicated in respiratory disease.
  • European Patent Application No. 0399320 disclosed glass fibres having a high physiological solubility.
  • the refractoriness of the fibres disclosed in these various prior art documents varies considerable.
  • the maximum service temperature of any of these disclosed fibres (when used as refractory insulation) is up to 815°C (1500°F).
  • Service temperature for refractory insulation is definable in many ways but to be consistent with the above mentioned International Patent Applications this application shall mean by service temperature that temperature at which the fibre shows acceptable shrinkage (maximum of 5% linear shrinkage after exposure to temperature for 24 hours) and at which the fibre has not appreciably suffered through excessive sintering or softening.
  • inorganic refractory fibres are glasses and so may be defined as liquids having an exceedingly high viscosity (but still liable to flow).
  • inorganic refractory fibres are glasses and so may be defined as liquids having an exceedingly high viscosity (but still liable to flow).
  • fibres are elongate and so have a high surface area per unit volume.
  • reduction of surface area is a means of reducing the surface energy of a material, when the glass becomes fluid enough it will flow so as to reduce surface area. This flow results in a coarsening and shortening of the fibres and so to shrinkage, and in the extreme results in disruption of the fibres into separate particles.
  • the second mechanism leading to shrinkage is that at elevated temperatures glasses may crystallise to form one or more crystal phases. Usually these crystal phases have a smaller molar volume than the glasses from which they crystallise and so shrinkage results.
  • Some fibres are known for which the molar volume of the crystalline form exceeds that of the glass (for example Al 2 O 3 /SiO 2 glassy fibres may crystallise to form mullite crystals). In these cases the expansion due to crystallisation may oppose the shrinkage caused by viscous flow.
  • refractory insulation inorganic refractory fibres are used in several forms.
  • the fibres may be supplied as a bulk material, but in this form the fibres are difficult to handle for many applications.
  • the fibre may be supplied as a blanket.
  • Blanket fibre is generally made by a process of sucking fibre from air onto a conveyor to form a blanket. Because the fibres tend to be aligned parallel to the conveyor surface they can separate easily. Accordingly the blanket fibres are secured together by adding a binder to lock the fibres together, or by needling the blanket, or both. In needling needles are passed through the thickness of the blanket to push and draw fibres to lie transverse to the blanket and so tie the fibres together.
  • binders are usually resins, such as phenolic resins, they burn off on first firing. There is a desire to reduce the amount of such binders used both because of possible health implications in handling, and because the combustion products may affect the strength of the fibres. Thus needled blanket is usually preferred.
  • the fibres may also be supplied as blocks, generally made from assembled layers of inorganic fibre blanket.
  • needled fibre blanket formed from inexpensive materials, being soluble in saline solutions, and having a maximum service temperature in the range 900°C-1200°C.
  • refractory oxide fibres are made by several methods all of which involve the formation of a melt of oxides and the subsequent fiberisation of the melt by e.g. spinning or blowing.
  • the melt of oxide material is often formed by electrical discharge melting of the constituent raw materials.
  • the applicants, in manufacture of a CaO/MgO/SiO 2 refractory oxide fibre encountered problems due to the necessity of handling CaO. These problems were discovered to be due to the moisture content of CaO as commercially available.
  • One of the problems of use of CaO is the outgasing that results upon melting and this led at the least to a porous melt pool which caused fluctuations in the melt current; in the extreme the outgasing and explosive. Additionally use of CaO appeared to cause accelerated attack on the melt electrodes. Also CaO is a difficult and corrosive material to handle.
  • a series of fibres were made of the compositions shown in Table 1. These fibres were melt spun by using a vertical spinning system of the type known for making inorganic fibres. Also shown in Table 1 are the compositions of some comparative commercially available inorganic oxide fibres and glass fibres.
  • the fibres SW-A, SW-A1, SW-A2, SW-B1, SW-B2 and SW-B3 were tested for solubility by the following method.
  • the fibre was first chopped in the following manner. 2.5 g of fibre (deshotted by hand) was liquidised with 250 cm 3 of distilled water in a domestic Moulinex (Trade Mark) food blender for 20 seconds. The suspension was then transferred to a 500 cm 3 plastic beaker and allowed to settle after which as much liquid as possible was decanted and the remaining liquid removed by drying in an oven at 110°C.
  • the solubility test apparatus comprised a shaking incubator water bath, and the test solution had the following composition:- Compound Name Grams NaCl Sodium chloride 6.780 NH 4 Cl Ammonium chloride 0.540 NaHCO 3 Sodium bicarbonate 2.270 Na 2 HPO 4 .H 2 O Disodium hydrogen phosphate 0.170 Na 3 C 6 H 5 O 7P .2H 2 O Sodium citrate dihydrate 0.060 H 2 NCH 2 CO 2 H Glycine 0.450 H 2 SO 4 s.g. 1.84 Sulphuric acid 0.050 The above materials were diluted to 1 litre with distilled water to form a physiological-like saline solution.
  • the centrifuge tube was removed and centrifuged at ⁇ 4500 revs/minute for approximately 5 minutes.
  • Supernatant liquid was then drawn off using a syringe and hypodermic needle.
  • the needle was then removed from the syringe, air expelled from the syringe, and the liquid passed through a filter (0.45 micron cellulose nitrate membrane filter paper [WCN type from Whatman Labsales Limited]) into a clean plastic bottle.
  • the liquid was then analysed by atomic absorption using a Thermo Jarrell Ash Smith - Hiefje II machine.
  • Aluminium may be measured directly from the sample without dilution. Standards of 1.0, 5.0 and 10.0 ppm Al may be used. For calibration readings are multiplied by 1.8895 to convert from Al to Al 2 O 3 .
  • a standard Al atomic absorption solution (e.g. BDH 1000 ppm Al) was bought and diluted using an accurate pipette to the desired concentration. 0.1% KCl was added to prevent ionic interference.
  • Calcium may require dilutions on the sample before determination can be carried out (i.e. x 10 and x 20 dilutions). Dilutions must contain 0.1% KC1.
  • a standard Ca atomic absorption solution (e.g. BDH 1000 ppm Ca) was diluted with distilled water and an accurate pipette to give standards of 0.5, 4.0 and 10.0 ppm. 0.1% KCl is added to prevent ionic interference. To convert readings obtained from Ca to CaO a factor of 1.4 was used.
  • Magnesium may require dilutions on the sample before determinations can be made (i.e. x 10 and x 20). Add 0.1% KCl to each dilution. To convert Mg to MgO multiply by 1.658.
  • a standard Mg atomic absorption solution (e.g. BDH 1000 ppm Mg) was diluted with distilled water and an accurate pipette to give standards of 0.5, 1.0 and 10.0 ppm Mg. 0.1% KCl was added to prevent ionic interference.
  • the user is primarily concerned with the solubility of the fibre as received as it is in this condition that most handling occurs; as received both SW-A2 and SW-B3 fibres have extremely high solubility. Even after exposure to 800°C and 1000°C these fibres have solubilities much higher than other high temperature use fibres.
  • Table 5 shows the results of Shrinkage tests on all the test fibres and on some of the comparative fibres. These results were obtained by proposed ISO standard ISO/TC33/SC2/N220 (equivalent to British Standard BS 1920, part 6,1986) with some modifications to account for small sample size.
  • the method in summary comprises the manufacture of vacuum cast preforms, using 75g of fibre in 500cm 3 of 0.2% starch solution, into a 120 x 65mm tool. Platinum pins (approx 0.1-0.3mm diameter) were placed 100 x 45mm apart in the 4 corners.
  • Table 9 (three pages) below gives the compositions of a series of melts, ranked on silica content, and showing the shrinkage figure after exposure to 1000°C for 24 hours (1st column) and 800°C for 24 hours (2nd column). These shrinkages were measured by the same method as the shrinkages given above but measurements were made with a travelling microscope with a digital linear scale accurate to ⁇ 5 ⁇ m. It can clearly be seen that all fibres with a silica content of less than 58% have a shrinkage at 1000°C of greater than 3.5% save two (B3-3 and 708). These fibres, together with some fibres with a silica content of greater than 58% although showing a reasonable figure at 1000°C, show a very poor figure at 800°C.
  • compositions with an SiO 2 content of greater than 70% appear to fiberise poorly. This may be because such compositions have two liquids in the melt as may be appreciated from Fig.1 CYCLIC SHRINKAGE (LINEAR) (%) Product 1000°C 1100°C 24h at 1000°C No. cycles 58 42 CRBT 2.0 2.7 1.9 CWBT 15.0 13.3 12.1 SW-A2 0.33 2.0 1.3 SW-B3 1.00 1.67 1.1 SW-B3 0.33 0.67 1.1 Accuracy: + or - 0.33%
  • compositions B3-6A, A2-25, A2-24, A2-23, B3-2A, B3-3A, A2-19, and 932 There are several anomalies, namely compositions B3-6A, A2-25, A2-24, A2-23, B3-2A, B3-3A, A2-19, and 932. All of these have an SiO 2 content of > 58% but a high shrinkage.
  • the Al 2 O 3 content is important. From their studies it appears that the maximum Al 2 O 3 content lies somewhere between 2.57% and 3.97%. The applicants have found that with increasing alumina levels the first material to crystallise is calcium aluminate and this possibly forms a liquid phase that assists flow and hence shrinkage.
  • Table 10 shows, for the same compositions as Table 9, 24 hour solubilities for each major constituent. It can be seen that all of the compositions have high solubilities.
  • the raw materials used to make the melt comprised:- Pennine Darlington Heavy Magnesia (#200) MgO 92.60% CaO 1.75% Fe 2 O 3 0.04% SiO 2 0.20% Cl 0.25% SO 3 0.70% LOI 4.50% Partek's Finnish Low Iron Wollastonite (#200) (U.K.
  • Fibre was produced by blowing (although spinning and other methods can be used). 2 runs were performed with different blowing conditions.
  • this feature of the invention is not limited to saline soluble fibres and any oxide fibre that contains both calcium and silicon can advantageously be made with a calcium silicate, wollastonite being merely an example of such a silicate.

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  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Organic Chemistry (AREA)
  • Glass Compositions (AREA)
  • Inorganic Fibers (AREA)
  • Building Environments (AREA)
  • Inorganic Insulating Materials (AREA)
  • Ceramic Products (AREA)
  • Chemical Or Physical Treatment Of Fibers (AREA)
EP93902385A 1992-01-17 1993-01-15 Use of saline soluble inorganic fibres as insulation material Expired - Lifetime EP0621858B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP01106342A EP1179513A1 (en) 1992-01-17 1993-01-15 Saline soluble inorganic fibres

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
GB929200993A GB9200993D0 (en) 1992-01-17 1992-01-17 Saline soluble inorganic fibres
GB9200993 1992-01-17
GB929224612A GB9224612D0 (en) 1992-11-24 1992-11-24 Manufacture of calcium and silicon-containing refractory oxide fibres
GB9224612 1992-11-24
PCT/GB1993/000085 WO1993015028A1 (en) 1992-01-17 1993-01-15 Saline soluble inorganic fibres

Related Child Applications (1)

Application Number Title Priority Date Filing Date
EP01106342A Division EP1179513A1 (en) 1992-01-17 1993-01-15 Saline soluble inorganic fibres

Publications (2)

Publication Number Publication Date
EP0621858A1 EP0621858A1 (en) 1994-11-02
EP0621858B1 true EP0621858B1 (en) 2001-12-19

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EP93902385A Expired - Lifetime EP0621858B1 (en) 1992-01-17 1993-01-15 Use of saline soluble inorganic fibres as insulation material
EP01106342A Ceased EP1179513A1 (en) 1992-01-17 1993-01-15 Saline soluble inorganic fibres

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US (1) US7259118B2 (enrdf_load_stackoverflow)
EP (2) EP0621858B1 (enrdf_load_stackoverflow)
JP (2) JP3630167B2 (enrdf_load_stackoverflow)
KR (1) KR100236883B1 (enrdf_load_stackoverflow)
CN (1) CN1042023C (enrdf_load_stackoverflow)
AT (1) ATE211122T1 (enrdf_load_stackoverflow)
AU (2) AU663155C (enrdf_load_stackoverflow)
BR (1) BR9305741A (enrdf_load_stackoverflow)
CA (1) CA2127357C (enrdf_load_stackoverflow)
CZ (1) CZ286812B6 (enrdf_load_stackoverflow)
DE (1) DE69331376T2 (enrdf_load_stackoverflow)
DK (1) DK0621858T3 (enrdf_load_stackoverflow)
ES (1) ES2168094T3 (enrdf_load_stackoverflow)
FI (1) FI943380L (enrdf_load_stackoverflow)
GB (2) GB2287934A (enrdf_load_stackoverflow)
HU (1) HU218828B (enrdf_load_stackoverflow)
IN (1) IN186395B (enrdf_load_stackoverflow)
MX (1) MX9300200A (enrdf_load_stackoverflow)
NO (1) NO942655L (enrdf_load_stackoverflow)
NZ (1) NZ246629A (enrdf_load_stackoverflow)
RU (1) RU2113420C1 (enrdf_load_stackoverflow)
SK (1) SK282182B6 (enrdf_load_stackoverflow)
WO (1) WO1993015028A1 (enrdf_load_stackoverflow)

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ES2168094T3 (es) 2002-06-01
AU663155C (en) 2005-12-15
CA2127357C (en) 2004-05-04
CA2127357A1 (en) 1993-08-05
FI943380A7 (fi) 1994-09-14
CN1042023C (zh) 1999-02-10
SK85694A3 (en) 1995-01-12
FI943380A0 (fi) 1994-07-15
MX9300200A (es) 1997-04-30
HK1001888A1 (en) 1998-07-17
KR940703787A (ko) 1994-12-12
DE69331376T2 (de) 2002-07-11
HU9402118D0 (en) 1994-09-28
RU2113420C1 (ru) 1998-06-20
AU3358493A (en) 1993-09-01
JPH07502969A (ja) 1995-03-30
CN1078218A (zh) 1993-11-10
EP0621858A1 (en) 1994-11-02
GB2277516B (en) 1995-11-22
HU218828B (hu) 2000-12-28
WO1993015028A1 (en) 1993-08-05
JP3630167B2 (ja) 2005-03-16
GB2277516A (en) 1994-11-02
HUT68033A (en) 1995-05-29
AU2717195A (en) 1995-09-28
EP1179513A1 (en) 2002-02-13
NZ246629A (en) 1997-07-27
DE69331376D1 (de) 2002-01-31
ATE211122T1 (de) 2002-01-15
NO942655D0 (no) 1994-07-14
NO942655L (no) 1994-07-14
GB9509871D0 (en) 1995-07-12
BR9305741A (pt) 1997-01-28
DK0621858T3 (da) 2002-04-15
GB9414171D0 (en) 1994-08-31
RU94037553A (ru) 1996-05-20
KR100236883B1 (ko) 2000-01-15
GB2287934A (en) 1995-10-04
AU663155B2 (en) 1995-09-28
CZ170094A3 (en) 1995-06-14
IN186395B (enrdf_load_stackoverflow) 2001-08-18
CZ286812B6 (en) 2000-07-12
FI943380L (fi) 1994-09-14
US20050014624A1 (en) 2005-01-20
SK282182B6 (sk) 2001-11-06
US7259118B2 (en) 2007-08-21
JP3753416B2 (ja) 2006-03-08
JP2001270737A (ja) 2001-10-02

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